Graphene Oxide: An All-in-One Processing ... - ACS Publications

Research Article www.acsami.org

Graphene Oxide: An All-in-One Processing Additive for 3D Printing Esther García-Tuñoń ,*,†,‡ Ezra Feilden,† Han Zheng,† Eleonora D’Elia,† Alan Leong,† and Eduardo Saiz† †

Centre for Advanced Structural Ceramics, Department of Materials, Imperial College London, Royal School of Mines, Prince Consort Road, South Kensington, London SW7 2BP, U.K. ‡ Materials Innovation Factory & School of Engineering, University of Liverpool, Harrison Hughes Building, Brownlow Hill, Liverpool L69 3GH, U.K. S Supporting Information *

ABSTRACT: Many 3D printing technologies are based on the development of inks and pastes to build objects through droplet or filament deposition (the latter also known as continuous extrusion, robocasting, or direct ink writing). Controlling and tuning rheological behavior is key for successful manufacturing using these techniques. Different formulations have been proposed, but the search continues for approaches that are clean, flexible, robust and that can be adapted to a wide range of materials. Here, we show how graphene oxide (GO) enables the formulation of water-based pastes to print a wide variety of materials (polymers, ceramics, and steel) using robocasting. This work combines flow and oscillatory rheology to provide further insights into the rheological behavior of suspensions combining GO with other materials. Graphene oxide can be used to manipulate the viscoelastic response, enabling the formulation of pastes with excellent printing behavior that combine shear thinning flow and a fast recovery of their elastic properties. These inks do not contain other additives, only GO and the material of interest. As a proof of concept, we demonstrate the 3D printing of additive-free graphene oxide structures as well as polymers, ceramics, and steel. Due to its amphiphilic nature and 2D structure, graphene oxide plays multiple roles, behaving as a dispersant, viscosifier, and binder. It stabilizes suspensions of different powders, modifies the flow and viscoelasticity of materials with different chemistries, particle sizes and shapes, and binds the particles together, providing green strength for manual handling. This approach enables printing complex 3D ceramic structures using robocasting with similar properties to alternative formulations, thus demonstrating the potential of using 2D colloids in materials manufacturing. KEYWORDS: 2D colloids, processing, 3D printing, complex fluids, and oscillatory rheology

■

enhance the performance and flexibility of existing technologies.1,2,6 There are some similarities between graphene oxide (GO, also known as chemically modified graphene) and clay; both have large surface area and flake shape with a special distribution of functionalities on their geometry. Clay particles in water have different electrostatic charges on the basal plane and edges, which enables the formation of a “house of cards” arrangement and provides the plasticity required for shaping.1 Clay is also used as an additive in suspensions of other materials to provide the right viscoelastic behavior for processing; it has been recently used to formulate pastes for the 3D printing of composites.7,8 Due to their anisotropic nature, aqueous suspensions of clay particles can develop a liquid crystal character.9 On the other hand, GO, with its special combination of structure and surface chemistry, is an amphiphile. GO flakes on the basal plane are partly covered by hydrophilic functionalities (hydroxyls, carboxyl, and epoxy groups); carboxyl groups are also distributed throughout the edges,

INTRODUCTION Progress in colloidal processing is driven by the need for versatile and universal approaches to build increasingly complex parts and devices. The challenge is to manipulate the rheology of suspensions to fit specific processing techniques. Clay, the wet processing archetype, has been used for thousands of years to form ceramics, from pottery and art to advanced structural applications. Clay has a unique structure and chemistry that allows the formulation of water-based suspensions with ideal viscoelastic behavior for shaping in a way that cannot be done with any other natural material. The need to replicate this behavior and extrapolate it to other materials has driven the development of colloidal processing.1,2 This relatively new scientific field studies the basic science behind the formulation of stable suspensions and pastes, made by combining powders with different additives (dispersants, binders, surfactants, plasticizers, viscosifiers, etc.) to emulate the shaping behavior of natural clays. We can easily find a multitude of approaches, water or solvent based, designed to satisfy the needs for a specific material and manufacturing technique.3−5 However, additives have their own challenges and often demand further postprocessing steps. In addition, new formulations are continuously required to broaden the range of materials and © XXXX American Chemical Society

Received: May 31, 2017 Accepted: August 31, 2017

A

DOI: 10.1021/acsami.7b07717 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

Research Article

ACS Applied Materials & Interfaces

Figure 1. GO characterization: (a) Lateral flake size distribution obtained from >100 flakes from SEM and optical microscopy images using ImageJ. As exfoliated, the average flake size is 44 μm, breaking down to an average of 16 μm after ultrasonication. (b) Thermogravimetric analysis (of a concentrated GO slurry carried out in air) shows the water loss (95.5 wt %) up to 100 °C, and no residues at 500 °C as all the carbon was burnt out. (c) X-ray diffraction analysis of a suspension droplet dried in air, showing the characteristic peak for GO at 2θ ≈ 10°.45 (d) Raman spectroscopy analysis performed on a dry droplet of GO suspension, showing its characteristic bands (D at 1361 cm−1, G at 1598 cm−1, and a small shoulder around the 2D band at 2730 cm−1).38

while some regions on the basal plane remain unoxidized.10 The interactions between these moieties with water and across flakes (at pH ∼ 5 the hydroxyl functional groups in GO flakes are partly protonated,11,12 facilitating the formation of hydrogen bonds) enable the formulation of very stable, viscoelastic GO slurries and facilitate their arrangement in a liquid crystal structure.13,14 GO has been used in noncolloidal systems with ABS and PLA for 3D printing using fused deposition approaches.15 GO and composites have also been 3D-printed with the aid of additives and in some cases solvents.12,16,17 Despite the progress in the field, it is still necessary to develop flexible and robust processing approaches to bring advanced ceramics, 2D nanoparticles, and any other materials into additive manufacturing. This work focuses on the unique rheology of GO colloids in water, delving into their behavior in the absence of additives and, for the first time, reporting their multiple roles, enabling the processing and printing of other materials in water based systems. Here, we explore clay-GO similarities and demonstrate that it is possible to use GO to create clay-like suspensions from different materials. Our findings show that graphene oxide may well be one of the most versatile processing additives available, behaving simultaneously as dispersant, rheological modifier, and binder. It has the potential to simplify and enable the water-based wet processing of a wide range of materials from polymers to metals and ceramics, including highly anisotropic

particles whose suspensions are usually difficult to stabilize and manipulate. The unique behavior of graphene oxide in water can be used to tune the viscoelastic behavior of suspensions containing particles with very different chemistries, shapes, and sizes in a way that is not possible with other additives. This can be done at very low GO concentrations, with the added advantage that it can be either subsequently eliminated or retained during the postprocessing steps, thus potentially adding structural or functional properties to the final part. As a proof of concept, in this work, we used graphene oxide to formulate pastes for the additive manufacturing of 3D structures made of polymers, ceramics, or steel. The structure and properties of the printed parts were evaluated. These results open new, flexible, and scalable possibilities for materials processing, printing, and manufacturing.

■

MATERIALS AND METHODS

Materials. GO suspensions were prepared by the exfoliation of graphite using the modified Hummers method in a custom-built reactor designed to manipulate up to 5 L of concentrated acids.12 The suspensions were purified to remove residual salts and acids using repeated centrifugation at 9000 rpm (Thermo Scientific Sorvall LYNX 6000 Superspeed Centrifuge) and redispersion in double-distilled water. Nonexfoliated particles were removed by low speed centrifugation (1000 rpm). Washing/centrifugation cycles were carried out until the particle-free supernatants had a pH ∼ 6, typically occurring after 16 washing cycles. B


Research Article


Figure 2. Flow behavior and viscoelastic properties (G′, storage modulus) of GO oxide suspensions and pastes with increasing concentrations of GO flakes in the absence of additives. (a) The flow ramps show how the viscosity rapidly increases for diluted GO suspensions in water with concentrations between 0.1 and 0.6 vol %. (b) Histogram showing the effect of flake size (as prepared 44 μm vs after ultrasounds 16 μm) on the viscoelastic response of GO diluted suspensions with flakes with different lateral flake sizes and distributions (Figure 1). There is a slight drop of the storage modulus (G′) for a 0.1 vol % suspension prepared with small flakes, but as GO concentration increases, the effect of flake size on viscoelastic properties becomes insignificant. GO solutions with 0.6 vol % solids made with different flake sizes have similar values of G′. GO flakes were prepared for scanning electron microscopy (SEM) (LEO Gemini 1525) by drop-casting diluted GO solutions into silicon oxide substrates. Lateral dimensions of GO flakes were measured from SEM and optical microscopy (Axio Scope A1, Zeiss) images using ImageJ (size distribution histogram in Figure 1). Freeze-drying of a known volume of GO suspensions and weighing the dry monoliths gave an estimation of the GO content. The GO suspension and slurries were also characterized with thermogravimetric analysis (TGA), X-ray diffraction (XRD), and Raman spectroscopy (Figure 1). For XRD and Raman analyses, the as prepared GO suspension was drop-casted on a silicon single crystal substrate and a glass slide, respectively. Alumina powders (SMA6, Baikowski, FR) with an average diameter of 0.35 μm were sieved through 100 μm to remove large agglomerates. Alumina platelets (with a lateral size of ∼5 μm and thickness of ∼0.3 μm, Advanced Nano Technologies Ltd., Australia) were used as provided by the supplier. Silicon carbide powders (D50 = 0.45 μm, UF25, H. C. Starck, DE) were mixed with sintering aids (6 wt % alumina and 4 wt % yttria (Grade C, H. C. Starck, DE)) in methanol for 24 h with Si3N4 milling media in a roll mill, followed by drying in a rotary evaporator. PVA, polyvinyl alcohol: Mw (146 000−186 000), 99% hydrolyzed, Sigma-Aldrich, steel AISI 316L microspheres (D50 = 40 μm, AISI, United States). Rheology Study of GO Suspensions. The as prepared GO suspension with a concentration of 0.6 vol % was diluted 1:2 and 1:4 to evaluate the effect of flake concentration on viscosity and viscoelastic properties (Figure 2). Additionally, these suspensions were subjected to sonication using an ultrasound tip at 200W, 24kHHz, with amplitude of 60% and a pulse of 5 s for 30 min to break down the lateral size. Optical microscopy images (Axio Scope A1, Zeiss) were used to determine the lateral dimensions of these “small flakes” (Figure 1). These suspensions were used to evaluate the effect of flake size on rheological behavior (Figure 2). Shear controlled flow ramps were carried out in a TA HR1 rheometer using 2 different geometries (40 mm plate; and 60 mm cone with a truncation gap of 59 μm). Prior the oscillatory tests for the pastes, we confirmed that the use of these two different geometries (cone−plate and plate−plate) during flow tests leads to consistent results for the low concentrated suspensions. Paste Preparation. GO pastes were prepared by redispersing freeze-dried GO powders to increase concentration (method 1); alternatively, the slurry was concentrated by water evaporation in an oil bath at 70 °C (method 2). Both approaches led to concentrated GO pastes with good behavior for printing without the need of any other additive. A Thinky ARE-250 planetary mixer was used for both methods using several mixing cycles (2000 rpm for 2 min) in between small additions of freeze-dried GO powder or small amounts of

evaporated water to guarantee a homogeneous structure within the paste. A final defoaming step at 2200 rpm for 10 min was applied to all the samples to eliminate any remaining trapped air. The GO suspensions obtained after graphite exfoliation/cleaning/ centrifugation with a concentration of ∼0.6 vol % can be used directly as formulation base for ceramic powders, metals, and polymers with a wide range of particle sizes and shapes. These include: Al2O3 powders and platelets, SiC powders, PVA, and steel. To tune viscoelasticity and flow, additional freeze-dried powder was in some cases added to achieve the desired rheological behavior. In detail, the pastes reported in this work had the following concentrations. For the alumina platelets: paste 1 with 23 vol % platelets (0.8 vol % GO (23 mg/mL)) and paste 2 with 27 vol % Al2O3 platelets (1.1 vol % GO (33 mg/mL), GO/Al2O3 ratio (3/100 in weight)). For the SiC powders: 28.4 vol % SiC with 0.4 vol % GO (10 mg/mL). For the steel: 40.4 vol % with 0.4 vol % GO (19 mg/mL). PVA: 8.3 vol % PVA with 0.3 vol % GO (7 mg/mL). For comparative purposes, suspensions of steel and Al2O3 platelets and a solution of PVA in the absence of GO were also prepared to evaluate their printability and evaluate their viscoelastic responses. Rheology of Pastes. Oscillatory tests were carried out in a TA HR1 rheometer with temperature control (20 °C) and solvent trap cover using parallel plates. For concentrated pastes, the use of the plate geometry (ø = 40 mm) with a gap between 500 μm and 1 mm avoids jamming of particles. The structure of the pastes and its response to different stimuli was assessed using a sequence of five oscillatory steps while monitoring the viscoelastic properties (G′, G″). Step 1 determines their initial internal structure and stability with a gentle oscillation at low frequency (0.5 Hz) and strain (0.5%). Step 2 identifies structure changes with a frequency sweep (fixed strain at 0.5%, frequency from 0.5− to 50 Hz). Step 3 monitors the recovery after step 2 with a gentle oscillation at low frequency (0.5 Hz) and strain (0.5%). Step 4 identifies structure changes with strain and to measure yield stress and strain with an amplitude sweep (fixed frequency at 0.5 Hz, strain from 0.1 up to 50%). Step 5 checks the recovery of the internal structure immediately after the time sweep with a gentle oscillation at low frequency (0.5 Hz) and strain (0.5%). The waveform and Lissajous plots were monitored and recorded throughout all the steps (1−5) to identify nonlinear events during structure changes and track the quality of the data. The Lissajous graphs provide a visual tool to identify nonlinearities: large ellipsoids that get closer to a round shape mean the behavior is close to an ideal liquid (large area indicates that more energy is dissipated); when the ellipsoids thin and get closer to a line, then the system is getting closer to an ideal solid.18 Printing. Graphene oxide based pastes were used to print 3D objects using a robotic deposition device (Robocad 3.0, 3-D inks C


Research Article


Figure 3. Viscoelastic properties for GO suspensions and pastes: fingerprints (a) and effect of GO concentration on G′ (storage modulus, b) and yield stress (c). The more concentrated systems are printable (labeled 3D-printable in a). The storage modulus (b) and yield stress (c) increase with flake concentration following a power law, in agreement with existing literature on the subject.16,19,20,27 (d) Schematic showing the proposed assembly of GO flakes in water as concentration increases. Some of the GO flakes roll up, forming graphene oxide scrolls; both assemble into a 3D liquid crystal structure with a strong elastic response (a). Stillwater, OK) on a PTFE substrate at printing speeds between 6 and 12 mm s−1 through 510 μm nozzles (EFD, Nordson). A 40 mm leadin line was printed immediately before the start of each part to ensure a homogeneous flow as the parts were printed, including cylinders, grids, and 40 × 4 × 3 mm3 test bars. The temperature and humidity of the whole system were controlled by a custom built enclosure and a convection heater set to 23 °C while the measured humidity varied from 70 to 95%. Postprocessing. GO structures were frozen in liquid nitrogen and freeze-dried for 48 h (Freezone 4.5, Labconco Corporation) followed by thermal reduction at 900 °C for 1 h under 10% H2/90% Ar atmosphere. Printed parts (alumina, SiC, and steel) were dried over 24 h in a humidified enclosure to avoid cracking, followed by another drying step in a convection oven at 37 °C. Structures built with the alumina platelets paste were sintered in a tube furnace at 1550 °C under 10% H2/90% Ar atmosphere. Once dry, SiC printed parts were isostatically pressed at 300 MPa for 1 min at room temperature in an evacuated pouch using a Stanstead Fluid Power isostatic press and subsequently pressure-less sintered under Ar atmosphere in a graphite furnace using a powder bed (to avoid loss of material due to evaporation) at 2050 °C for 1 h at atmospheric pressure. All heating and cooling rates were 10 °C min−1. Characterization. The apparent density and porosity of the sintered scaffolds were measured by Archimedes’ method (Sartorius, YDK01, Goettingen, Germany) in water. The microstructure and chemical composition were studied by field emission scanning electron microscopy on a LEO Gemini 1525 FEGSEM equipped with an energy dispersive spectroscopy (EDS) microprobe (INCA Sight Oxford-instruments, UK). Samples were coated with a thin Cr layer previous to the observation. XRD patterns were collected using a PANanalytical XRD X’Pert Pro diffractometer operated at 40 kV and 40 mA in the 2θ range 5−35° with a step size of 0.0334° and a count

time at each step of 100 s. Raman spectroscopy was performed using a Renishaw RM2000 equipped with a 514 nm laser. Three point bending tests were carried out in a Zwick universal testing machine with a maximum load of 2 kN using a 20 mm bottom span and a displacement rate of 0.2 mm min−1. A standard four-point probe method was used for conductivity measurements. The current was generated via a benchtop PSU and kept at a constant direct current of 10 mA. Two electrodes were placed through the sample at constant distance to monitor the voltage drop through the sample. The results were derived via standard equations for electrical conductivity and resistivity in DC.

■

RESULTS AND DISCUSSION

Rheology and Printability of Graphene Oxide Suspensions and Pastes. Graphene oxide suspensions in water have shear thinning behavior (Figure 1a). The viscosity and viscoelastic properties of GO suspensions in water strongly depend on their concentrations (Figure 2a),9,19−21 which is very similar to water−clay systems.22,23 GO suspensions with low concentrations (≤0.1 vol % GO) have liquid-like behavior (G′ < G″) with small elastic component (G′ ∼ 7 Pa, Figure 2b). Previous studies state that for GO aqueous dispersions, lateral size and concentration have equal influence on viscosity.21 However, we found that in the range of this study (i.e., lateral flake size averages varying between 16 and 44 μm, Figure 1), the lateral size has a minor effect on the viscoelastic properties for diluted suspensions, and its effect becomes negligible as flake concentration increases (Figure 2b). At concentrations above 0.1 vol %, the GO flakes form a soft solid (G′ > G″) that breaks down and flows when certain yield stress is applied D


Research Article


Figure 4. Printed structures and oscillatory rheology of additive-free GO pastes. (a) Image of a structure printed to test the stiffness of the filaments across spans with increasing lengths. The filaments retain their shape well across spans up to 15 mm during printing, but they tend to deflect during drying for the larger gaps. (b) 3D printed cylinder made for bulk characterization of the paste after postprocessing (density and electrical conductivity). (c) Evolution of viscoelastic fingerprints for a GO paste without additives (3 vol % GO in water, which corresponds to 76 mg/mL). Including the waveform and Lissajous plots for some of the points. These graphs illustrate structure changes with frequency and strain. Frequency slightly increases the liquid-like behavior (frequency seep). The GO network breaks down and flows with a liquid-like behavior during the amplitude sweep.

(Figure 3a). Increasing the GO concentration above ∼2 vol % leads to a rapid rise of the solid-like component (G′, Figures 3a and b) due to the formation of a well-established and organized structure (Figure 3d). We found that in these GO slurries, some of the flakes tend to roll up, forming graphene oxide scrolls (Figure 3d). These changes in conformation, known as carbon nanoscrolls CNS, have been previously reported for other carbon materials.24−26 As the slurry becomes more concentrated, GO flakes arrange, forming a network,19 similarly to a liquid crystal.13 The increase in concentration results in a considerable increase of the elastic response with storage modulus (G′) values up to 100 kPa (for 3.5 vol % GO, Figure 3b) as well as an exponential increase of the yield stress up to 2300 Pa (Figure 3c). GO additive-free pastes with concentrations between ∼2.5 and 3.5 vol % (prepared either by redispersing freeze-dried GO powders or by evaporation) display the rheological properties and structure needed for robocasting (Figures 3 and 4). A comparison of the storage modulus (G′, Figure 3b) and yield stress (Figure 3c) of these pastes with other additive-free GO suspensions in literature16,19,20,27 confirms a consistent trend. Despite the differences in the chemistry and lateral size of the GO flakes (from 40016 and 600 nm19 to 44 μm (this work)) and the fact that the measurements were done using different settings, the dependence of the storage modulus and the yield stress with the GO content follows a similar power law in all cases (∼2.2 for the yield stress and ∼2.5−3 for the storage modulus, Figures 3b and c). Cylinders and other 3D shapes (Figures 4a and b) can be printed using these pastes. Thanks to their shear thinning behavior, they easily flow through small nozzles and quickly recover once the shear eases off, retaining the shape once

printed and supporting the layers on top (Figure 4a and b). A sequence of oscillatory stimuli in the rheometer provides insights into the structure, stability, and response to frequency and strain for the 3 vol % GO (76 mg/mL) paste (Figure 4). Its solid-like (G′ > G″) structure is very stable within the LVR at all times except for the transition to liquid-like at strains of 16%. In more detail, during step 1, the sinusoidal signal is free of background noise, and no nonlinear effects can be detected in the Lissajous graph, which has a clear ellipsoid shape. As frequency increases in step 2, a slight increase of the liquid-like component is detected (see phase between sinusoidal signals and Lissajous curve, Figure 4c), but still, the solid-like component dominates with linear behavior. The time sweep (step 3) shows how the paste immediately recovers its initial structure once the frequency is reduced to 0.5 Hz. During the amplitude sweep (step 4), as strain increases, the structure starts to break down, and nonlinear effects are detected in the sinusoidal signals and Lissajous graphs. The loss of structure and transition from solid-like to liquid-like takes place at a yield stress of 254 Pa and strain of 16%, corresponding with the transition to nonlinear behavior. This illustrates the structural changes of the paste as it travels through the nozzle during the printing process. The final time sweep (step 5) shows how the GO network quickly recovers (the signals and Lissajous curves correspond to the first point measured in this region). Although there is a slight increase of G″ comparing with initial values (also a bigger phase lag and a larger area within the Lissajous plot), G′ and G″ values are in the same order of magnitude as in the initial step. This illustrates the rebuild of the structure that recovers its initial elasticity with G′ values >10 000 Pa, facilitating the printing of filaments that retain their shape E


Research Article


Figure 5. (a) External surface of additive-free printed filaments of GO. (b) Image of the internal microstructure showing the formation of GO scrolls interconnecting the 3D network, in more detail at higher magnification (c). (d) Histogram showing the evolution of the ID/IG ratio after thermal treatment. Before any thermal treatment, both GO suspension and also the aerogel have wide D and G peaks with similar intensity. After thermal reduction (at 250 and 900 °C), the ID/IG ratio increases, confirming the recrystallization and reduction of GO to rGO. (e) Graph comparing the electrical conductivity of 3D printed cylinders using different water based formulations (responsive surfactants, hydrogel base F127, and no additives (NA)) as well as with other structures found in the literature made following different methods.12,16,28−37

additive-free GO slurries prepared by water evaporation (Figure 5c). Raman spectroscopy on reduced flakes at 250 and 900 °C confirm the increase of the ID/IG ratio (Figure 5d).38 Printed cylinders after reduction display the expected values of density and electrical conductivity (Figure 5e). Graphene Oxide as Printing Additive for a Polymer Solution (PVA). Besides additive-free printable and selfsupporting GO pastes, it is also possible to design GO-based printable formulations of a wide range of materials with different chemistries, shapes, and particle sizes. These pastes do not contain any further additives, only water, graphene oxide flakes, and the material of interest. We demonstrate the use of this approach with solutions (such as PVA polymers polyvinyl

(Figure 5a), is self-supporting and strong enough to support the layers on top. After postprocessing, the 3D printed GO parts have internal microstructure (Figures 5b and c) and functional properties similar to those made using alternative formulations (based in pH responsive surfactants (BCS)12 and hydrogels (F127)) and other assembling approaches besides 3D printing, including freezing and emulsion templating approaches of graphene, reduced graphene oxide, and other carbon materials (Figure 5e).16,28−37 Microstructural analyses reveal how at the microscale the flakes arrange in a porous 3D network (Figure 5b) and evidence the formation of graphene oxide scroll bridges across flakes (Figure 5c). The scroll formation is more noticeable for F


Research Article


Figure 6. GO aids the printing of PVA solutions. 3D printed PVA-GO cylinder and viscoelastic fingerprints for the PVA-GO paste (8 vol % PVA, 0.3 vol % GO in water). The structure of this paste is very stable (steady G′ and G″ values) and has a solid-like structure within the LVR at all times. As frequency increases in step 2, there is a considerable increase of the liquid-like component (see phase between sinusoidal signals and the increase of the area within the ellipsoid in the Lissajous plot), but still, the solid-like dominates with linear behavior. Step 3 shows how the paste immediately recovers its initial structure once the frequency is reduced to 0.5 Hz. The structure does not break down under the amplitude sweep (step 4), suggesting the formation of a true gel between PVA and GO.

Figure 7. Structural characterization of 3D printed steel made using GO as printing additive: (a) Image of a steel disc after drying; (b−e) FESEM images at different magnifications. (b) External surface of a 3D printed filament where the spheres are evenly distributed bonded by GO. (c−e) Morphological details of the GO/steel interactions: GO flakes wrap around the steel particles (c and e) and connect to other particles forming a 3D network. The images (c−e) illustrate this connection, which visually reminds us of the lamellipodia found in cells colonizing surfaces (d). A ∼3 μm steel sphere (e) is suspended in an empty space (in a fracture surface) hold by a GO nanoscroll that wraps around and connects it to a steel bigger particle.

rheological behavior, facilitating the viscoelasticity required for the printing process. All the pastes are shear thinning and have viscoelastic behavior with G′ dominating (i.e., solid like behavior); however, each of them has a unique viscoelastic fingerprint that depends on the intrinsic properties of the filler.

alcohol, Figure 6), and particulate systems such as ceramic powders (SiC and Al2O3) and platelets and even steel microspheres. Due to its two-dimensional nature and high surface area, the addition of GO at low concentration ranges (between 0.1 and 1 vol %) to other materials changes their G


Research Article

ACS Applied Materials & Interfaces PVA solutions (8 vol %) on their own do not exhibit adequate viscoelastic properties for robocasting (Supporting Information, Figures S1 and S2). PVA solutions have liquid-like behavior with low values of G′ ( G″). For comparative purposes, the viscoelastic fingerprints (frequency and amplitude sweeps) for all of them are compiled in Figure 13. Despite the similarities, each system has a unique viscoelastic fingerprint (Figures 13a and b). Their individual response is intimately related to the solid loading

this paste displays adequate printing behavior. The network breaks down and flows through the nozzle due to the shearthinning behavior and rebuilds with enough stiffness (G′ > G″, and G′ in the order of 5 kPa) to print bulk 3D objects, for example, bars for mechanical testing, cylinders, and lattices (Figures 11 and 12). Once dry, SiC 3D printed bars have strengths of ∼1 MPa measured in 3-point bending, proving that GO is also acting as a binder of SiC surfaces. During the mechanical tests of these green structures, some GO flakes were bridging across the cracks, which suggests that additional reinforcement mechanisms might be taking place. However, the visual inspection of fractured surfaces in the SEM did not provide clear insights on the SiC/GO interactions (Figure 11c). Sintered SiC bars (2050 °C for 2 h) have a final density of 3.21 J


Research Article


Figure 12. Structural characterization of sintered SiC structures 3D printed using GO as the only additive. (a and b) SiC objects after pressureless sintering under Ar atmosphere at 2050 °C. (c) Fracture surface of a SiC sintered bar (2050 °C for 2 h) after mechanical testing showing good density and transgranular fracture. Sintered SiC bars have a final density of 3.21 g/cm3 (96.4% of the theoretical) and bending strengths of ∼212 MPa.

(which is defined by the intrinsic properties of the filler such as size, specific surface, and density) and highly likely due to the different nature of the interactions at the GO/material interfaces. In general, larger particles with smooth surfaces (steel and alumina platelets) allow higher solid contents due to the smaller specific surface area. This results in pastes with more stable structures, linear behavior, and larger values for G′ (Figure 13c). On the other hand, small anisotropic nonoxide particles (as SiC) lead to more complex internal structures with nonlinear behavior. This might be due to the contribution of different factors: the friction between small and irregular particles with a narrow distribution limits the solid loading, packing, and flow, and different interactions at the GO/SiC interface. Despite these differences, all of the experiments carried out with these very diverse materials confirm that the GO flakes are simultaneously playing different roles: (1) as dispersant, stabilizing particle suspensions of oxide (Al2O3) and nonoxide (SiC) ceramics and steel; (2) as viscosifier, providing the rheological behavior needed for robocasting; and (3) as binder, binding the particles and forming a stable structure after drying, providing printed shapes that are stable and easy to handle manually once dry. Using GO instead of other currently available formulations in literature (for example, hydrogels (F127), pH responsive surfactants, clays, or PEI) provides key advantages for materials manufacturing: simplicity, versatility, flexibility, scalability, and robustness. Here, GO is the only additive, while other formulations in literature require multiple ingredients and even the use of solvents.16,17,43 GO’s multifunctional surface chemistry plays complementary roles as processing enabler for different materials. Unlike clay (that provides electrostatic interactions), GO can establish hydrophobic, steric, and noncovalent (i.e., hydrogen bonds) interactions with other materials. Due to its large surface area, very small amounts of GO can completely shift the viscoelastic response while, for example, the standard concentration for F127 hydrogels is ∼25 wt %,42,44 which can become a problem during postprocessing steps. For example, the burnout of large amounts of volatile organics restricts the use of spark plasma sintering (SPS) for

structures made with F127 formulations. Additionally, thanks to its 2D structure, GO flakes (unlike clay particles) can twist, bend, and roll up, establishing multiple interactions in a 3D network. Lastly, GO colloids provide formulations with robust viscoelastic responses that are independent of external stimuli; on the contrary, F127, pH responsive surfactants, and PEI are sensitive to temperature and pH.42,43

■

CONCLUSIONS

We showed that there are key similarities between graphene oxide and clay. Both exhibit a flake-like shape with different functionalities on their edges and faces that result in the formation of particle networks connected by electrostatic interactions for clay and noncovalent interactions for GO. As a result, as for clay, graphene oxide aids the formulation of pastes for wet processing, providing the right viscoelastic response to a very wide range of materials with different chemistries, particle morphologies (from particles, platelets and fibers to microspheres), and sizes (from nanometers to tens of micrometers). Graphene oxide is an all-in-one additive, acting as a dispersant, viscosifier, printing aid, and binder, leading to formulations containing only three components: graphene oxide, water, and the material of interest. After printing, graphene oxide can be eliminated (e.g., by a thermal treatment in an oxidizing atmosphere) or retained to potentially add functionality to the final materials by designing postprocessing steps to facilitate in situ reduction, for example, spark plasma sintering. While it could be argued that graphene based materials are very expensive additives, this is true only for pristine graphene or CVD graphene. Graphene oxide (exfoliated graphite) can be produced on a large scale, and only small amounts are required for this application. This opens up multiple possibilities for materials manufacturing, in particular for robocasting of complex structures and composites as well as new processing approaches for other traditional and modern techniques such as casting, injection, and roll-to-roll processes. K


Research Article


■

Stability of steel particles in water (Figure S1); printability of PVA, Al2O3, and steel in water without GO (Figure S1); additional information and rheological fingerprints with and without GO for PVA (Figure S2), steel (Figures S3 and S4), Al2O3 platelets (Figures S5 and S6), and SiC (Figure S7) (PDF)

AUTHOR INFORMATION

Corresponding Author

*E-mail: [email protected]. ORCID

Esther García-Tuñoń : 0000-0001-9507-4501 Notes

The authors declare no competing financial interest.

■

ACKNOWLEDGMENTS E.G.T. and E.S. acknowledge the EPSRC Grant Graphene 3D Networks (EP/K01658X/1) and Manufacture Using Advanced Powder Processes (MAPP EP/P006566/1). E.F. acknowledges the CASC (Centre for Advanced Structural Ceramics) industrial consortium. E.D. acknowledges funding from the Defence Advanced Research Projects Agency (DARPA), “BioInspired Self-Healing Materials Based on Ceramic−Polyurethane Hybrid Composites”. A.L. acknowledges PETRONAS (Graphene Composites for Pipelines).

■ ■

REFERENCES

(1) Lewis, J. A. Colloidal Processing of Ceramics. J. Am. Ceram. Soc. 2000, 83 (10), 2341−2359. (2) Greil, P. Advanced Engineering Ceramics. Adv. Eng. Mater. 2002, 4 (5), 247−254. (3) Ahn, B. Y.; Duoss, E. B.; Motala, M. J.; Guo, X.; Park, S. I.; Xiong, Y.; Yoon, J.; Nuzzo, R. G.; Rogers, J. A.; Lewis, J. A. Omnidirectional Printing of Flexible, Stretchable, and Spanning Silver Microelectrodes. Science 2009, 323 (5921), 1590−1593. (4) Smay, J. E.; Gratson, G. M.; Shepherd, R. F.; Cesarano, J.; Lewis, J. A. Directed Colloidal Assembly of 3D Periodic Structures. Adv. Mater. 2002, 14 (18), 1279−1283. (5) Heule, M.; Vuillemin, S.; Gauckler, L. J. Powder-Based Ceramic Meso- and Microscale Fabrication Processes. Adv. Mater. 2003, 15 (15), 1237−1245. (6) Evans, J. Seventy Ways to Make Ceramics. J. Eur. Ceram. Soc. 2008, 28 (7), 1421−1432. (7) Compton, B. G.; Lewis, J. A. 3D-Printing of Lightweight Cellular Composites. Adv. Mater. 2014, 26 (34), 5930−5935. (8) Sydney Gladman, A.; Matsumoto, E. A.; Nuzzo, R. G.; Mahadevan, L.; Lewis, J. A. Biomimetic 4D Printing. Nat. Mater. 2016, 15 (4), 413−418. (9) Michot, L. J.; Bihannic, I.; Maddi, S. Liquid−Crystalline Aqueous Clay Suspensions. Proc. Natl. Acad. Sci. U. S. A. 2006, 103, 16101− 16104. (10) Kim, F.; Cote, L. J.; Huang, J. Graphene Oxide: Surface Activity and Two-Dimensional Assembly. Adv. Mater. 2010, 22 (17), 1954− 1958. (11) Konkena, B.; Vasudevan, S. Understanding Aqueous Dispersibility of Graphene Oxide and Reduced Graphene Oxide Through P KaMeasurements. J. Phys. Chem. Lett. 2012, 3 (7), 867−872.

Figure 13. Comparing the viscoelasticity of selected formulations made using GO as the only additive: pure GO (3 vol % GO, 76 mg/ mL), SiC powders (0.4 vol % GO, 10 mg/mL), PVA (0.3 vol % GO, 7 mg/mL), Al2O3 platelets (1.1 vol % GO, 33 mg/mL), and steel microspheres (0.4 vol % GO, 19 mg/mL). Each system has a different response according to the intrinsic properties of the material. The frequency sweep (a) and amplitude sweep (b) provide information on the structure and viscoelastic response that is compiled in chart c for comparative purposes. (c) Histogram comparing the viscoelastic properties: storage modulus, G′ (obtained from a time sweep at 0.5 Hz and 0.5% strain), and yield stress (obtained from graph b). The chart also displays their total solid loading (vol %) and GO content (vol %). Note that PVA-GO is the only system that forms a true gel; its combined structure does not break down with strain, and its behavior remains within the LVR as strain increases. On the contrary, steel−GO and ceramics−GO systems break down at strains that range between 3 and >20% depending on the material (b and c). In general, they have an initial linear behavior before the transition to liquid-like (except for SiC-GO, Figure S3).

■

ABBREVIATIONS GO, graphene oxide PVA, poly(vinyl alcohol) CMG, chemically modified graphene rGO, reduced graphene oxide PEI, poly(ethylenimine)

ASSOCIATED CONTENT

S Supporting Information *

The Supporting Information is available free of charge on the ACS Publications website at DOI: 10.1021/acsami.7b07717. L


Research Article

ACS Applied Materials & Interfaces (12) Garcıa-Tuñoń , E.; Barg, S.; Franco, J.; Bell, R.; D’Elia, E.; Maher, R. C.; Guitián, F.; Saiz, E. Printing in Three Dimensions with Graphene. Adv. Mater. 2015, 27 (10), 1688−1693. (13) Xu, Z.; Gao, C. Aqueous Liquid Crystals of Graphene Oxide. ACS Nano 2011, 5 (4), 2908−2915. (14) Liu, Y.; Xu, Z.; Gao, W.; Cheng, Z.; Gao, C. Graphene and Other 2D Colloids: Liquid Crystals and Macroscopic Fibers. Adv. Mater. 2017, 29, 1606794. (15) Wei, X.; Li, D.; Jiang, W.; Gu, Z.; Wang, X.; Zhang, Z.; Sun, Z. 3D Printable Graphene Composite. Sci. Rep. 2015, 5, 1−7. (16) Zhu, C.; Han, T.; Duoss, E. B.; Golobic, A. M. Highly Compressible 3D Periodic Graphene Aerogel Microlattices. Nat. Commun. 2015, 6, 6962. (17) Román-Manso, B.; Figueiredo, F. M.; Achiaga, B.; Barea, R.; Pérez-Coll, D.; Morelos-Gómez, A.; Terrones, M.; Osendi, M. I.; Belmonte, M.; Miranzo, P. Electrically Functional 3D-Architectured Graphene/SiC Composites. Carbon 2016, 100, 318−328. (18) Hyun, K.; Wilhelm, M.; Klein, C. O.; Cho, K. S.; Nam, J. G.; Ahn, K. H.; Lee, S. J.; Ewoldt, R. H.; McKinley, G. H. A Review of Nonlinear Oscillatory Shear Tests: Analysis and Application of Large Amplitude Oscillatory Shear (LAOS). Prog. Polym. Sci. 2011, 36 (12), 1697−1753. (19) Vallés, C.; Young, R. J.; Lomax, D. J.; Kinloch, I. A. The Rheological Behaviour of Concentrated Dispersions of Graphene Oxide. J. Mater. Sci. 2014, 49 (18), 6311−6320. (20) Naficy, S.; Jalili, R.; Aboutalebi, S. H.; Gorkin, R. A., III; Konstantinov, K.; Innis, P. C.; Spinks, G. M.; Poulin, P.; Wallace, G. G. Graphene Oxide Dispersions: Tuning Rheology to Enable Fabrication. Mater. Horiz. 2014, 1 (3), 326−331. (21) Bao, C.; Zhang, H.; Wilkie, C. A.; Bi, S.; Tang, X. Z.; Wu, J.; Yang, J. On the Dispersion Systems of Graphene-Like TwoDimensional Materials: From Fundamental Laws to Engineering Guidelines. Carbon 2016, 107 (C), 774−782. (22) Coussot, P. Structural Similarity and Transition From Newtonian to Non-Newtonian Behavior for Clay-Water Suspensions. Phys. Rev. Lett. 1995, 74 (20), 3971−3974. (23) Mourchid, A.; Lecolier, E.; Van Damme, H.; Levitz, P. On Viscoelastic, Birefringent, and Swelling Properties of Laponite Clay Suspensions: Revisited Phase Diagram. Langmuir 1998, 14 (17), 4718−4723. (24) Dong, X.; Xing, G.; Chan-Park, M. B.; Shi, W.; Xiao, N.; Wang, J.; Yan, Q.; Sum, T. C.; Huang, W.; Chen, P. The Formation of a Carbon Nanotube−Graphene Oxide Core−Shell Structure and Its Possible Applications. Carbon 2011, 49 (15), 5071−5078. (25) Liu, Z.; Xue, Q.; Tao, Y.; Li, X.; Wu, T.; Jin, Y.; Zhang, Z. 2 Modeling and Methods. Phys. Chem. Chem. Phys. 2015, 17, 3441− 3450. (26) Jayasena, B.; Subbiah, S.; Reddy, C. D. Formation of Carbon Nanoscrolls During Wedge-Based Mechanical Exfoliation of HOPG. J. Micro Nano-Manuf. 2014, 2 (1), 011003. (27) Li, W.; Li, Y.; Su, M.; An, B.; Liu, J.; Su, D.; Li, L.; Li, F.; Song, Y. Printing Assembly and Structural Regulation of Graphene Towards Three-Dimensional Flexible Micro-Supercapacitors. J. Mater. Chem. A 2017, 5, 3639. (28) Barg, S.; Perez, F. M.; do Vale Pereira, P.; Ni, N.; Maher, R.; Garcia-Tunon, E.; Agnoli, S.; Eslava, S.; Mattevi, C.; Saiz, E. Mesoscale Assembly of Chemically Modified Graphene Into Complex Cellular Networks. Nat. Commun. 2014, 5, 1−10. (29) Guan, L.-Z.; Gao, J.-F.; Pei, Y.-B.; Zhao, L.; Gong, L.-X.; Wan, Y.-J.; Zhou, H.; Zheng, N.; Du, X.-S.; Wu, L.-B.; Jiang, J.-X.; Liu, H.-Y.; Tang, L.-C.; Mai, Y.-W. Silane Bonded Graphene Aerogels with Tunable Functionality and Reversible Compressibility. Carbon 2016, 107 (C), 573−582. (30) Lin, Y.; Liu, F.; Casano, G.; Bhavsar, R.; Kinloch, I. A.; Derby, B. Pristine Graphene Aerogels by Room-Temperature Freeze Gelation. Adv. Mater. 2016, 28 (36), 7993−8000. (31) Zou, J.; Liu, J.; Karakoti, A. S.; Kumar, A.; Joung, D.; Li, Q.; Khondaker, S. I.; Seal, S.; Zhai, L. Ultralight Multiwalled Carbon Nanotube Aerogel. ACS Nano 2010, 4 (12), 7293−7302.

(32) Zhang, X.; Sui, Z.; Xu, B.; Yue, S.; Luo, Y.; Zhan, W.; Liu, B. Mechanically Strong and Highly Conductive Graphene Aerogel and Its Use as Electrodes for Electrochemical Power Sources. J. Mater. Chem. 2011, 21 (18), 6494−6497. (33) Worsley, M. A.; Kucheyev, S. O.; Satcher, J. H., Jr. Mechanically Robust and Electrically Conductive Carbon Nanotube Foams. Appl. Phys. Lett. 2009, 94, 073115. (34) Chen, Z.; Ren, W.; Gao, L.; Liu, B.; Pei, S.; Cheng, H.-M. Three-Dimensional Flexible and Conductive Interconnected Graphene Networks Grown by Chemical Vapour Deposition. Nat. Mater. 2011, 10 (6), 424−428. (35) Qiu, L.; Liu, J. Z.; Chang, S.; Wu, Y.; Li, D. Biomimetic Superelastic Graphene-Based Cellular Monoliths. Nat. Commun. 2012, 3, 1241. (36) de la Osa, G.; Pérez-Coll, D.; Miranzo, P.; Osendi, M. I.; Belmonte, M. Printing of Graphene Nanoplatelets Into Highly Electrically Conductive Three-Dimensional Porous Macrostructures. Chem. Mater. 2016, 28 (17), 6321−6328. (37) Qian, Y.; Ismail, I. M.; Stein, A. Ultralight, High-Surface-Area, Multifunctional Graphene-Based Aerogels From Self-Assembly of Graphene Oxide and Resol. Carbon 2014, 68 (C), 221−231. (38) Cançado, L. G.; Jorio, A.; Ferreira, E. H. M.; Stavale, F.; Achete, C. A.; Capaz, R. B.; Moutinho, M. V. O.; Lombardo, A.; Kulmala, T.; Ferrari, A. C. Quantifying Defects in Graphene via Raman Spectroscopy at Different Excitation Energies. Nano Lett. 2011, 11, 3190− 3196. (39) Gao, H.; He, J.; Yang, R.; Yang, L. Characteristic Rheological Features of High Concentration PVA Solutions in Water with Different Degrees of Polymerization. J. Appl. Polym. Sci. 2010, 116, 2734−2741. (40) Feilden, E.; Ferraro, C.; Giuliani, F.; Vandeperre, L.; Saiz, E. Progress in Novel and Unexpected Areas. Mater. Today 2016, 19 (9), 544. (41) García-Tuñoń , E.; Machado, G. C.; Schneider, M.; Barg, S.; Bell, R. V.; Saiz, E. Complex Ceramic Architectures by Directed Assembly of “Responsive”Particles. J. Eur. Ceram. Soc. 2017, 37 (1), 199−211. (42) Feilden, E.; García-Tuñoń , E.; Giuliani, F.; Saiz, E.; Vandeperre, L. Journal of the European Ceramic Society. J. Eur. Ceram. Soc. 2016, 36 (10), 2525−2533. (43) Lewis, J. A.; Smay, J. E.; Stuecker, J.; Cesarano, J. Direct Ink Writing of Three-Dimensional Ceramic Structures. J. Am. Ceram. Soc. 2006, 89 (12), 3599−3609. (44) Goyos-Ball, L.; García-Tuñon, D. E.; Fernández-García, E.; Díaz, R.; Fernández, A.; Prado, C.; Saiz, E.; Torrecillas, R. Journal of the European Ceramic Society. J. Eur. Ceram. Soc. 2017, 37 (9), 3151− 3158. (45) Marcano, D. C.; Kosynkin, D. V.; Berlin, J. M.; Sinitskii, A.; Sun, Z.; Slesarev, A.; Alemany, L. B.; Lu, W.; Tour, J. M. Improved Synthesis of Graphene Oxide. ACS Nano 2010, 4 (8), 4806−4814.

M


Graphene Oxide: An All-in-One Processing ... - ACS Publications

Recommend Documents